AU2006308245B2 - Method for producing hot strip with a multiphase structure - Google Patents

Method for producing hot strip with a multiphase structure Download PDF

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Publication number
AU2006308245B2
AU2006308245B2 AU2006308245A AU2006308245A AU2006308245B2 AU 2006308245 B2 AU2006308245 B2 AU 2006308245B2 AU 2006308245 A AU2006308245 A AU 2006308245A AU 2006308245 A AU2006308245 A AU 2006308245A AU 2006308245 B2 AU2006308245 B2 AU 2006308245B2
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Prior art keywords
strip
cooling
hot
austenite
range
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AU2006308245A2 (en
AU2006308245A1 (en
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Christian Bilgen
Wolfgang Hennig
Joachim Ohlert
August Sprock
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SMS Siemag AG
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SMS Siemag AG
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
    • C21D8/0415—Rapid solidification; Thin strip casting
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • C21D1/20—Isothermal quenching, e.g. bainitic hardening
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
    • C21D8/0215—Rapid solidification; Thin strip casting
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
    • C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Metal Rolling (AREA)
  • Heat Treatment Of Steel (AREA)

Description

TRANSLATION (HM-827PCT-original): WO 2007/048,497 Al PCT/EP2006/009,755 METHOD FOR PRODUCING HOT-ROLLED STRIP WITH A MULTIPHASE MICROSTRUCTURE The invention concerns a method for producing hot-rolled strip that consists of TRIP (transformation-induced plasticity) steel with a multiphase microstructure and with both high strength values and outstanding deformation properties, where the TRIP steel strip is produced from the hot-rolled state by controlled cooling after the last rolling stand. The adjustment of the microstructure is a complex matter in TRIP steels, since, besides ferrite and bainite, a third phase is present in the form of retained austenite or, after a subsequent deformation, in the form of martensite. TRIP steels are now usually produced in a two-stage heat cycle. The starting material is hot-rolled or cold-rolled strip, in which an approximately 50% a - 50% y initial microstructure is adjusted. Due to the higher solubility of carbon in austenite, austenite has a higher carbon concentration. After the annealing treatment, rapid cooling is carried out past the ferrite and pearlite range into the bainite range, in which 1 isothermal conditions are maintained for some time. The austenite is partially transformed to bainite, and at the same time the remainder of the austenite becomes further enriched with carbon. In this way, the martensite start temperature M, is reduced to values below ambient temperature, and consequently the retained austenite also continues to exist at ambient temperature. The final microstructure consists of 40 70% ferrite, 15-40% bainite, and 5-20% retained austenite. The special effect of TRIP steels is the transformation of the metastable retained austenite to martensite when external plastic deformation occurs. The transformation of the austenite to martensite is accompanied by an increase in volume, which is supported not just by the austenite alone but rather by the surrounding microstructural components as well. The ferritic matrix is plasticized, which in turn results in greater strain hardening and leads overall to higher plastic elongations. Steels produced in this way have an extraordinary combination of high strength and high ductility, which makes them suitable especially for use in the automobile industry. The process management described above which is presently used mostly for the industrial production of TRIP steels, is complicated and expensive due to the additional annealing and 2 cooling treatment after the rolling operation, which is the reason that attempts have been made to produce these TRIP steels directly as hot-rolled strip in industrial production plants for hot strip production. For example, EP 1 396 549 Al discloses a method for producing pearlite-free hot-rolled steel strip with TRIP properties in a continuously running operational process, in which a steel melt, which contains, in addition to iron and unavoidable impurities, 0.06-0.3% C; 0.1 3.0% Si; 0.3-1.1% Mn (with the total amount of Si and Mn being 1.5-3.5%); 0.005-0.15% of at least one of the elements Ti or Nb as an essential component; and optionally one or more of the following elements: max. 0.8% Cr; max. 0.8% Cu; and max. 1.0% Ni, is cast into thin slabs, which are annealed at 1,000 1,200 0 C for an annealing time of 10-60 minutes in an annealing furnace, starting from a run-in temperature of 850-1,050 0 C. After descaling, the thin slabs are finish hot rolled in the range of 750-1,000*C and then cooled to a coiling temperature of 300-530 0 C. The controlled cooling is carried out in two stages at a cooling rate of the first stage of at least 150 K/s with a cooling interruption of 4-8 seconds. Alternatively, it is proposed that the controlled cooling be carried out continuously at a cooling rate of 10-70 K/s without a holding interruption. Finally, a third possibility 3 is proposed, in which the cooling is controlled in such a way that the hot rolled strip is cooled in a first phase to a temperature of about 80 0 C above coiling temperature within 1-7 seconds and is then cooled to coiling 5 temperature by air cooling. Besides the prescribed process management, the presence of Ti and/or Nb is important, since these elements remain in solution until the start of the hot rolling and upon their subsequent precipitation, improve, among other properties, the grain 10 fineness of the hot-rolled strip and increase the retained austenite content and its stability. Using this prior art as a point of departure, the objective of the invention is to specify a method which allows simpler and more economical production of 15 TRIP steels in existing plants and in which an annealing treatment and the addition of alloying elements that are otherwise not absolutely necessary can be eliminated. The present invention relates to a method for producing hot-rolled strip having TRIP (transformation 20 induced plasticity) properties in a thin-slab continuous casting and rolling plant (CSP plant), the composition of the strip comprising from 0.12 to 0.25% C; from 0.05 to 1.8% Si; 4 865894 1 (GHKatters) 24/06/10 from 1.0 to 2.0% Mn; the reminder Fe and unavoidable impurities, wherein the method includes: " finishing rolling of the hot-rolled strip for 5 adjusting a very fine austenite grain (d < 8 pm) which is carried out at temperatures in the range of 770 to 830 0 C, just above Ar 3 in the range of metasble austenite; and " two-stage cooling of the hot rolled strip immediately after the finishing rolling, the two-stage 10 cooling includes cooling the strip to a strip temperature of about 650 to 730'C in which the strip enters the ferrite range and holding the strip temperature for a period so as transform austenite of the strip to at least 40% ferrite, and further cooling the strip to a strip temperature in 15 the range of bainite formation of about 320 to 480*C; whereby the method produces a steel microstructure which consists of 40-70% ferrite, 15-45% bainite, and 5-20% retained austenite. In contrast to the usual procedure that was 20 described earlier, in accordance with the invention, in an austenitically finish rolled hot strip, the typical microstructure for a TRIP steel is adjusted immediately after the last rolling stand by a two-stage cooling operation in the cooling line. In this connection, the 5 865894_1 [G)0tatters) 24/08/10 adjustment of the appropriate microstructure requires extensive process know-how as well as very exact maintenance of the necessary process parameters. Due to the narrow tolerance range for the 5 5A 865894 1 (GHMattero) 24108/10 production of TRIP steels on hot wide strip mills, since the introduction of thin-slab continuous casting and rolling technology, a plant configuration has been available which provides much better conditions for the direct production of TRIP steels than hot-rolled strip, compared to conventional hot-rolled strip mills. Due to the high degree of uniformity of temperature over the thickness, width, and length of the strip, TRIP steels with constant mechanical properties can be reproducibly produced in this way. Due to the short length of the conventional cooling lines used in this process in existing continuous casting and rolling mills, the production of hot-rolled strip with TRIP microstructure is possible only with a special rolling and cooling strategy. The rolling strategy of the invention is used for adjusting a very fine austenite grain (d < 8 pm) during the last deformation, which has an accelerating effect on the ferrite transformation in the subsequent cooling line. Therefore, the finish rolling of the strip takes place at temperatures of 770-830 0 C, just above Ar 3 in the range of metastable austenite. The successful implementation of the cooling strategy makes it absolutely necessary to maintain certain limits of 6 chemical composition in order to realize the desired degree of transformation within the short total cooling time that is available. Therefore, the chemical analysis proposed for the production of TRIP steels varies within the following limits: 0.12-0.25% C, 0.05-1.8% Si, 1.0-2.0% Mn, the remainder Fe and customary accompanying elements. The cooling strategy involves two-stage cooling with the option of using different cooling rates in each stage. The start of the holding time at temperatures of 650-730 0 C is determined by the entry of the cooling curve into the ferrite range. The desired transformation of the austenite to at least 40% ferrite then takes place during the following brief cooling interruption. The holding time is then immediately followed by the second cooling stage, in which the hot-rolled strip is cooled to a temperature of 320-480 0 C. The transformation of austenite to at least 15% bainite takes place at this temperature. In addition to the use of a short holding time, the cooling strategy is determined by an exactly defined, predetermined cooling rate for the two cooling stages. This cooling rate is V = 30-150 K/s and preferably V = 50-90 K/s, depending on the geometry of the hot-rolled strip and the chemical composition of the steel grade that is used. In 7 regard to these cooling rates, it should be noted that a cooling rate less than 30 K/s is not possible due to the small amount of time that is available in the conventional cooling line of a continuous casting and rolling plant, and that cooling rates greater than 150 K/s likewise cannot be realized in cooling lines of this type, which consist of a succession of water cooling zones spaced a certain distance apart. The hot-rolled strip produced with the method of the invention with TRIP steel properties for different strength levels with an elastic limit tensile strength ratio Rpo.
2 / Rm in the range of 0.45-0.75 has the following combinations of tensile strength Rm and percentage elongation after fracture A: Rm = 600-700 MPa =' A > 25% Rm = 700-800 MPa = A > 23% Rm = 800-900 MPa => A > 21% Rm = 900-1,000 MPa = A > 18% Rm > 1,000 MPa => A > 15% Further details and advantages of the invention are explained in greater detail below with reference to the specific embodiment of the invention illustrated in the accompanying drawings. 8 -- Figure 1 shows a CSP plant. -- Figure 2 shows a modified cooling line of the CSP plant. -- Figure 3 shows cooling curves for a dual-phase steel and a TRIP steel in a TTT diagram. Figure 1 shows the layout of a conventional CSP plant 1 schematically. In the illustrated example, it comprises the following main components in the direction of conveyance (from left to right in the drawing): the casting installation with two strands 2, the strand guides 3, the soaking furnaces 4 with a furnace transverse conveyor 5, a multiple-stand rolling mill 6, the cooling line 10, and coilers 8. Figure 2 shows a modified cooling line 10 of a CSP plant 1, which is necessary for carrying out cooling in accordance with the invention and is already known from EP 1 108 072 B1, which describes a method for producing dual-phase steel. This modified cooling line 10 of the CSP plant 1 is installed downstream of the last finish rolling stand 6'. The cooling line 10 has several successive water cooling zones 1117, 12 that are spaced a certain distance apart and can be automatically controlled. The water cooling zones 1117, 12 are equipped with water spray heads 13, which evenly spray the 9 upper and lower surfaces of the hot-rolled strip 7 with a specific amount of water. The positioning of the water cooling zones 1117, 12 within the cooling line 10, their number, their spacing, and the number of water spray heads 13 per water cooling zone 1117, 12 are chosen in such a way that the desired cooling rate of the two cooling stages can be variably adjusted in advance in order to achieve optimum adaptation of the water cooling zones 1117, 12 to the cooling conditions that are to be adjusted. Automatic control of the amount of water sprayed thus makes it possible, even during the cooling operation, to make any necessary change in the cooling rate. An additional water cooling zone 12 is installed a greater distance from the last water cooling zone 117 of the first cooling stage than the distance between the individual zones of water cooling zones 1117. The second cooling stage is carried out in this additional water cooling zone 12. In this water cooling zone 12, in contrast to the water cooling zones 1117 of the first cooling stage, there is a significantly larger number of water spray heads 13 in order to carry out forced intensive cooling over a shorter distance. The distance between the last water cooling zone 117 of the first cooling stage and the water cooling zone 12 of the 10 second cooling stage is chosen sufficiently large to obtain the holding time necessary to achieve transformation of the austenite to at least 40% ferrite, as prescribed by the invention, at the predetermined strip speed. Figure 3 shows a TTT diagram with the transformation lines for ferrite, pearlite, and bainite and with the temperature lines (20, 21, 22, 24) for Ac 3 , Aci, and M,. Horizontal shift arrows 27 for the transformation lines and vertical shift arrows 28 for the temperature lines show the effect of existing or added alloying elements on the position of these transformation and temperature lines in the TTT diagram. The cooling curve 25 for the production of a dual phase steel and the cooling curve 26 for the production of a TRIP steel in accordance with the invention are plotted in this TTT diagram as examples. At approximately the same start temperature (above Ac 3 ) at the start of cooling and approximately the same holding time temperature (above Ac 1 ), a significantly different microstructural composition is obtained due to the different courses of the cooling and the different compositions of the initial steels. According to the plotted cooling curve 25 for the dual-phase steel, the cooling curve 25 passes only into the ferrite range and ends below the martensite start temperature line 22, which is well 11 above room temperature 23, so that, as desired, a dual microstructure that consists only of ferrite and martensite is obtained. On the other hand, the cooling curve 26 for the production of a TRIP steel in accordance with the invention passes first through the ferrite range and then through the bainite range and ends above the martensite start temperature line 24, which is now below room temperature 23, so that transformation to martensite during cooling does not take place, and, in accordance with the invention, a microstructure is obtained that consists of ferrite, bainite, and some retained austenite. 12 LIST OF REFERENCE NUMBERS 1 CSP plant 2 casting installation with two strands 3 strand guide 4 soaking furnace 5 furnace transverse conveyor 6 multiple-stand rolling mill 6 6' last rolling stand 7 hot-rolled strip 8 coiler 9 temperature measurement 10 cooling line 111.7 water cooling zones 12 water cooling zone 13 water spray heads 20 Ac 3 temperature line 21 Aci temperature line 22 martensite start temperature line for a dual-phase steel 23 room temperature line 24 martensite start temperature line for a TRIP steel 25 cooling curve for a dual-phase steel 13 26 cooling curve for a TRIP steel 27 horizontal shift arrows of the transformation lines 28 vertical shift of the temperature lines 5 It is to be understood that, if any prior art publication is referred to herein, such reference does not constitute an admission that the publication forms a part of the common general knowledge in the art, in Australia or any other country. 10 14 965894_1 (GHatter) 24/08/10

Claims (6)

1. A method for producing hot-rolled strip having TRIP (transformation-induced plasticity) properties in a 5 thin-slab continuous casting and rolling plant (CSP plant), the composition of the strip comprising from 0.12 to 0.25% C; from 0.05 to 1.8% Si; from 1.0 to 2.0% Mn; 10 the reminder Fe and unavoidable impurities, wherein the method includes: " finishing rolling of the hot-rolled strip for adjusting a very fine austenite grain (d < 8 pm) which is carried out at temperatures in the range of 770 to 830 0 C, 15 just above Ar 3 in the range of metasble austenite; and " two-stage cooling of the hot rolled strip immediately after the finishing rolling, the two-stage cooling includes cooling the strip to a strip temperature of about 650 to 730*C in which the strip enters the ferrite 20 range and holding the strip temperature for a period so as transform austenite of the strip to at least 40% ferrite, and further cooling the strip to a strip temperature in the range of bainite formation of about 320 to 480*C; whereby the method produces a steel 15 865894_1 (GWHatters) 24/08/10 microstructure which consists of 40-70% ferrite, 15-45% bainite, and 5-20% retained austenite.
2. The method in accordance with Claim 1, wherein the cooling rate is V = 30-150 K/s, depending on the 5 chemical composition of the steel grade that is used and on the geometry of the hot-rolled strip.
3. The method in accordance with Claim 1, wherein the cooling rate is V= 50-90 K/s depending on the chemical composition of the steel grade that is used and on the 10 geometry of the hot-rolled strip.
4. The method in accordance with Claim 1, wherein the controlled two-stage cooling of the hot-rolled strip is carried out in a cooling line that consists of a succession of water cooling zones spaced a certain 15 distance apart.
5. The method in accordance with any one of claims 1 to 4, wherein the composition of the strip further comprises any one or a combination of: chromium, niobium, aluminium, phosphorus, molybdenum, boron, nickel and 20 titanium.
6. A hot-rolled strip with TRIP steel properties, characterized by a chemical composition within the following limits: 0.12-0.25% C; 0.05-1.8% Si; 1.0-2.0% Mn; the remainder Fe and customary accompanying elements; 16 865894_1 (GHMatters) 24/08/10 the steel strip comprising 40-70% ferrite, 15-45% bainite and 5-20% austenite, the steep strip having an elastic limit tensile strength ratio RPO. 2 / R, in the range of 0.45-0.75; and combinations of tensile strength Rm and 5 elongation after fracture A in accordance with the following: Rm = 600-700 MPa => A > 25% Rm = 700-800 MPa = A > 23% Rm = 800-900 MPa = A > 21% 10 Rm = 900-1,000 MPa => A > 18% Rm > 1,000 MPa = A > 15%. 17 865894 1 (GWMatters) 24/08/10
AU2006308245A 2005-10-25 2006-10-10 Method for producing hot strip with a multiphase structure Ceased AU2006308245B2 (en)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
DE102005051052A DE102005051052A1 (en) 2005-10-25 2005-10-25 Process for the production of hot strip with multiphase structure
DE102005051052.3 2005-10-25
PCT/EP2006/009755 WO2007048497A1 (en) 2005-10-25 2006-10-10 Method for producing hot strip with a multiphase structure

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AU2006308245A1 AU2006308245A1 (en) 2007-05-03
AU2006308245A2 AU2006308245A2 (en) 2008-06-19
AU2006308245B2 true AU2006308245B2 (en) 2010-09-30

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US (1) US20090214377A1 (en)
EP (1) EP1954842A1 (en)
JP (1) JP5130221B2 (en)
KR (1) KR20080063307A (en)
CN (1) CN101297049B (en)
AU (1) AU2006308245B2 (en)
BR (1) BRPI0617753A2 (en)
CA (1) CA2625564A1 (en)
DE (1) DE102005051052A1 (en)
RU (1) RU2398028C2 (en)
TW (1) TW200724690A (en)
UA (1) UA90436C2 (en)
WO (1) WO2007048497A1 (en)
ZA (1) ZA200802524B (en)

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DE102010050647A1 (en) * 2009-11-21 2011-05-26 Sms Siemag Aktiengesellschaft Plant and method for casting and rolling metal
CN102133579B (en) * 2010-01-27 2013-05-01 中国钢铁股份有限公司 Steel blank hot rolling process reducing generation of etch pit
US9896736B2 (en) 2010-10-22 2018-02-20 Nippon Steel & Sumitomo Metal Corporation Method for manufacturing hot stamped body having vertical wall and hot stamped body having vertical wall
MX361834B (en) 2010-10-22 2018-12-18 Nippon Steel & Sumitomo Metal Corp Steel sheet and steel sheet production process.
MX359051B (en) 2010-10-22 2018-09-13 Nippon Steel & Sumitomo Metal Corp Process for producing hot stamp molded article, and hot stamp molded article.
WO2012064129A2 (en) * 2010-11-10 2012-05-18 (주)포스코 Method for manufacturing high-strength cold-rolled/hot-rolled trip steel having a tensile strength of 590 mpa grade, superior workability, and low mechanical-property deviation
EP2730666B1 (en) * 2011-07-06 2018-06-13 Nippon Steel & Sumitomo Metal Corporation Method for producing a cold-rolled steel sheet
KR20140068186A (en) * 2011-09-13 2014-06-05 타타 스틸 이즈무이덴 베.뷔. High strength hot dip galvanised steel strip
CZ303949B6 (en) * 2011-09-30 2013-07-10 Západoceská Univerzita V Plzni Method of achieving TRIP microstructure in steels by deformation heat
ES2746285T5 (en) * 2012-03-30 2022-12-19 Voestalpine Stahl Gmbh Cold rolled high strength steel sheet and process for producing said steel sheet
CN102586562B (en) * 2012-03-30 2013-08-21 河北钢铁集团有限公司 Production process for shock-proof disaster-relieving hot rolled transformation-induced plasticity (TRIP) steel plates
CZ304832B6 (en) * 2013-04-13 2014-11-26 Západočeská Univerzita V Plzni Heat treatment process of TRIP steel half-finished products
CN103898404B (en) * 2014-04-28 2015-12-09 莱芜钢铁集团有限公司 A kind of vanadium micro-alloying hot-rolled transformation induction plasticity steel and preparation method
CN104233092B (en) * 2014-09-15 2016-12-07 首钢总公司 A kind of analysis of producing hot rolled TRIP and preparation method thereof
MX2017008622A (en) * 2015-02-20 2017-11-15 Nippon Steel & Sumitomo Metal Corp Hot-rolled steel sheet.
CN105063309B (en) * 2015-07-31 2017-11-17 首钢总公司 A kind of method for improving low-carbon microalloy hardness of steel
WO2017109538A1 (en) 2015-12-21 2017-06-29 Arcelormittal Method for producing a steel sheet having improved strength, ductility and formability
WO2017109540A1 (en) * 2015-12-21 2017-06-29 Arcelormittal Method for producing a high strength steel sheet having improved ductility and formability, and obtained steel sheet
CN106048176B (en) * 2016-06-06 2019-01-08 日照宝华新材料有限公司 Method based on ESP bar strip continuous casting and rolling flow path production low-carbon hot-rolling TRIP steel
CN105821190B (en) * 2016-06-06 2019-01-08 日照宝华新材料有限公司 Method based on carbon analysis of producing hot rolled TRIP in the production of ESP bar strip continuous casting and rolling flow path
CN109563580A (en) 2016-08-05 2019-04-02 新日铁住金株式会社 Steel plate and coated steel sheet
KR101917448B1 (en) * 2016-12-20 2018-11-09 주식회사 포스코 High strength hot-rolled steel sheet having excellent weldability and ductility, and mathod for manufacturing same
CN108531811B (en) * 2018-05-16 2020-05-01 东北大学 Preparation method of cast-rolled TRIP steel thin strip
RU2689348C1 (en) * 2018-06-26 2019-05-27 Публичное акционерное общество "Северсталь" (ПАО "Северсталь") Method for production of hot-rolled high-strength rolled metal
AT525283B1 (en) * 2021-10-29 2023-02-15 Primetals Technologies Austria GmbH Method for producing a dual-phase steel strip in a combined casting and rolling plant, a dual-phase steel strip produced using the method and a combined casting and rolling facility
CN114645187A (en) * 2022-01-29 2022-06-21 安阳钢铁股份有限公司 Non-quenched and tempered 950 MPa-grade high-strength strapping steel and production method thereof
CN115976310A (en) * 2022-10-31 2023-04-18 昆明理工大学 Particle-reinforced high-strength bainite medium-temperature forged steel and preparation method thereof
CN115976396B (en) * 2022-12-30 2024-04-30 包头钢铁（集团）有限责任公司 High-strength corrosion-resistant hot rolled steel strip Q550NQR1 for container and production method thereof

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19911287C1 (en) * 1999-03-13 2000-08-31 Thyssenkrupp Stahl Ag Process for producing a hot strip
US6328826B1 (en) * 1999-07-30 2001-12-11 Usinor Method of fabricating “TRIP” steel in the form of thin strip, and thin strip obtained in this way
US20030084973A1 (en) * 1999-11-12 2003-05-08 Usinor Process for the production of a strip of hot rolled steel of very high strength, usable for shaping and particularly for stamping

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE3851371T3 (en) * 1987-06-03 2004-04-29 Nippon Steel Corp. Hot-rolled, high-strength steel sheet with excellent formability.
US6190469B1 (en) * 1996-11-05 2001-02-20 Pohang Iron & Steel Co., Ltd. Method for manufacturing high strength and high formability hot-rolled transformation induced plasticity steel containing copper
BE1011149A3 (en) * 1997-05-12 1999-05-04 Cockerill Rech & Dev Steel ductile high elastic limit and method for manufacturing steel.
JP2000087141A (en) * 1998-09-10 2000-03-28 Nkk Corp Production of thin high tensile hot rolled steel strip containing residual austenite
JP3081197B1 (en) * 1999-02-17 2000-08-28 株式会社神戸製鋼所 High strength steel sheet with excellent workability and fatigue properties
CA2387322C (en) * 2001-06-06 2008-09-30 Kawasaki Steel Corporation High-ductility steel sheet excellent in press formability and strain age hardenability, and method for manufacturing the same
JP3764411B2 (en) * 2002-08-20 2006-04-05 株式会社神戸製鋼所 Composite steel sheet with excellent bake hardenability

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE19911287C1 (en) * 1999-03-13 2000-08-31 Thyssenkrupp Stahl Ag Process for producing a hot strip
US6328826B1 (en) * 1999-07-30 2001-12-11 Usinor Method of fabricating “TRIP” steel in the form of thin strip, and thin strip obtained in this way
US20030084973A1 (en) * 1999-11-12 2003-05-08 Usinor Process for the production of a strip of hot rolled steel of very high strength, usable for shaping and particularly for stamping

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